EP1660693B1 - Procede de production d'un element constitutif profile trempe - Google Patents

Procede de production d'un element constitutif profile trempe Download PDF

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Publication number
EP1660693B1
EP1660693B1 EP04736386.6A EP04736386A EP1660693B1 EP 1660693 B1 EP1660693 B1 EP 1660693B1 EP 04736386 A EP04736386 A EP 04736386A EP 1660693 B1 EP1660693 B1 EP 1660693B1
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EP
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Prior art keywords
zinc
coating
oxygen
corrosion protection
protection layer
Prior art date
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EP04736386.6A
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German (de)
English (en)
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EP1660693A1 (fr
Inventor
Martin Fleischanderl
Siegfried Kolberger
Josef Faderl
Gerald Landl
Anna Elisabeth Raab
Herbert Eibensteiner
Werner BRANDSTÄTTER
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Voestalpine Krems Finaltechnik GmbH
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Voestalpine Krems Finaltechnik GmbH
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Priority claimed from AT0120303A external-priority patent/AT412878B/de
Priority claimed from AT12022003A external-priority patent/AT412403B/de
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/62—Quenching devices
    • C21D1/673—Quenching devices for die quenching
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/02—Stamping using rigid devices or tools
    • B21D22/04—Stamping using rigid devices or tools for dimpling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • C23C2/29—Cooling or quenching
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
    • C23C2/36—Elongated material
    • C23C2/40—Plates; Strips
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D5/00—Electroplating characterised by the process; Pretreatment or after-treatment of workpieces
    • C25D5/34—Pretreatment of metallic surfaces to be electroplated
    • C25D5/36—Pretreatment of metallic surfaces to be electroplated of iron or steel
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D5/00—Electroplating characterised by the process; Pretreatment or after-treatment of workpieces
    • C25D5/48—After-treatment of electroplated surfaces
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2221/00—Treating localised areas of an article
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2251/00—Treating composite or clad material
    • C21D2251/02—Clad material
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T29/00—Metal working
    • Y10T29/49—Method of mechanical manufacture
    • Y10T29/4998—Combined manufacture including applying or shaping of fluent material
    • Y10T29/49982—Coating
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T29/00—Metal working
    • Y10T29/49—Method of mechanical manufacture
    • Y10T29/49995—Shaping one-piece blank by removing material
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12785—Group IIB metal-base component
    • Y10T428/12792—Zn-base component
    • Y10T428/12799—Next to Fe-base component [e.g., galvanized]
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/31504—Composite [nonstructural laminate]
    • Y10T428/31678—Of metal

Definitions

  • the invention relates to a method for producing a hardened profile component with cathodic corrosion protection and to a hardened metallic profile component with cathodic corrosion protection.
  • Low alloy steel sheets are not resistant to corrosion after being produced by suitable forming steps, either by hot rolling or cold rolling. This means that after a relatively short time and due to the humidity at the surface, oxidation occurs.
  • a corrosion protection layer is a layer produced on a metal or in the near-surface region of a metal, which consists of one or more layers. Multi-layer coatings are also referred to as corrosion protection systems.
  • Possible corrosion protection layers are, for example, organic coatings, inorganic coatings and metallic coatings.
  • the purpose of metallic corrosion protection layers is to transfer the properties of the support material to the steel surface for as long as possible. Accordingly, the choice of an effective metallic corrosion protection requires the knowledge of the corrosion-chemical relationships in the system steel / coating metal / attacking medium.
  • the coating metals can be electrochemically nobler or electrochemically less noble than steel.
  • the respective coating metal protects the steel only through the formation of protective layers.
  • barrier protection As soon as the surface of the coating metal has pores or was injured, a "local element" forms in the presence of moisture, in which the base partner is attacked by the metal to be protected.
  • the more noble coating metals include tin, nickel and copper.
  • Metallic protective layers are applied by various methods. Depending on the metal and process, the connection of the steel surface is chemical, physical or mechanical and ranges from alloy formation and diffusion to adhesion and mere mechanical clamping.
  • the metallic coatings should have similar technological and mechanical properties as steel and behave similarly to steel or mechanical deformations or plastic deformations. The coatings should therefore not be damaged during forming and also affected by forming operations.
  • the metal to be protected is immersed in molten metal melts.
  • corresponding alloy layers are formed at the phase boundary steel-coating metal.
  • An example of this is the hot dip galvanizing.
  • Hot dip galvanizing the steel strip is passed through a zinc bath, the zinc bath having a temperature of around 450 ° C.
  • Hot-dip galvanized products have high corrosion resistance, good weldability and formability, and their main applications are the construction, automotive and household appliance industries.
  • electrodeposited metal coatings i. the electrolytic, so under current passage deposition of metallic coatings of electrolytes.
  • electrolytic coating is also possible with such metals, which can not be coated by melt-dip process.
  • Conventional layer thicknesses in electrolytic coating are usually between 2.5 and 10 microns, they are thus generally lower than in enamel dip coatings.
  • Some metals, e.g. Zinc also allow thick film coatings with electrolytic coating.
  • Electrolytically galvanized sheets are mainly used in the automotive industry, because of the high surface quality, these sheets are used above all in the outer skin area. They have good formability, weldability and storability as well as good paintable and matt surfaces.
  • the surface of the plate is scaled by heating, so that after forming and hardening the sheet surface must be cleaned, for example by sandblasting. Then the sheet is trimmed and possibly punched necessary holes.
  • the sheets have a very high hardness in the mechanical processing and therefore the processing is complicated and in particular a high tool wear exists.
  • WO 03/035922 A1 & EP 1439240 A1 discloses a method for producing a hardened profile component made of steel with cathodic corrosion protection, wherein a galvanized steel sheet is warmed up, then heated to an austenitizing temperature and then hot-press molded.
  • the Zn coating melt may contain elements such as 0.08-0.4% Al.
  • the US 6,564,604 B2 The object of the invention is to provide steel sheets which are subsequently subjected to a heat treatment, and a method for producing parts by press-hardening these coated steel sheets. In this case, it should be ensured despite the increase in temperature that the steel sheet is not decarburized and the surface of the steel sheet is not oxidized before, during and after the hot pressing or the heat treatment.
  • an alloyed intermetallic mixture should be applied to the surface before or after punching, which should provide protection against corrosion and decarburization and also can provide a lubricating function.
  • this document proposes to use a conventional, apparently electrolytically applied zinc layer, wherein this zinc layer is to convert with the steel substrate in a subsequent Austenit atmosphere the sheet substrate in a homogeneous Zn Fe Fe alloy layer.
  • This homogeneous layer structure is confirmed by microscopic images. Contrary to previous assumptions, this coating is said to have a mechanical resistance that prevents it from melting. In practice, however, such an effect does not show.
  • the use of zinc or zinc alloys should provide cathodic protection of the edges when cuts are present.
  • the US 6,564,604 B2 a coating is specified which consists of 50% to 55% aluminum and 45% to 50% zinc with possibly small amounts of silicon.
  • a coating is not new in itself and known under the brand name Galvalume®. It is stated that the coating metals zinc and aluminum with iron should form a homogeneous zinc-aluminum-iron alloy coating. In the case of this coating, it is disadvantageous that sufficient cathodic corrosion protection is no longer achieved here, but the predominant barrier protection which is achieved with this is not sufficient when used in the press hardening process, since partial surface damage to the surface is unavoidable.
  • the method described in this document is unable to solve the problem that, in general, zinc-based cathodic corrosion coatings are not suitable for protecting steel sheets which are to be subjected to a heat treatment after coating and may also be subjected to another shaping or Ümform suits.
  • a method for producing a sheet metal component wherein the sheet on the surface should have an aluminum layer or an aluminum alloy layer.
  • a sheet provided with such coatings is to be subjected to a press hardening process, giving as possible coating alloys an alloy with 9-10% silicon, 2-3.5% iron, balance aluminum with impurities and a second alloy with 2-4% iron and the rest aluminum with impurities.
  • Such coatings are known per se and correspond to the coating of a hot-dip aluminized steel sheet. In such a coating is disadvantageous in that only a so-called barrier protection is achieved. The moment that such a barrier layer is damaged or cracked in the Fe-Al layer, the base material, in this case the steel, is attacked and corroded. A cathodic protective effect is absent.
  • the DE 102 46 614 A1 therefore proposes a coating as a metal or a metal alloy by means of a galvanic coating process in organic, non-aqueous solution, wherein a particularly suitable and therefore preferred coating material is aluminum or an aluminum alloy.
  • a particularly suitable and therefore preferred coating material is aluminum or an aluminum alloy.
  • zinc or zinc alloys would be suitable.
  • Such a coated sheet can then be cold preformed and hot finished molded.
  • this method has the disadvantage that an aluminum coating, even if it was applied electrolytically, no longer offers corrosion protection in case of damage to the surface of the finished component, since the protective barrier has been broken.
  • an electrodeposited zinc coating it is disadvantageous that during heating for hot forming, the zinc is largely oxidized and no longer available for cathodic protection. Under a protective gas atmosphere, the zinc evaporates.
  • a method for the production of metal profile components for motor vehicles is known.
  • starting material provided in strip form is fed to a roll forming unit and formed into a rolled section.
  • at least partial areas of the rolled section are to be heated inductively to a temperature required for hardening and then quenched in a cooling unit.
  • the rolled sections are cut to form the profile components.
  • a particular advantage of roll forming is to be seen in the low production costs due to the high processing speed and low compared to a press tool costs.
  • a special heat-treatable steel is used for the profile component.
  • partial regions of the starting material may also be inductive, prior to entry into the rolling profiling unit, to those required for hardening Temperature heated and quenched before cutting the rolled section in a cooling unit.
  • the cutting must take place already in the hardened state, which is problematic due to the high hardness of the material.
  • the cut-to-length profile components have to be cleaned or descaled and after the ignition a corrosion piece coating has to be applied, whereby such corrosion piece coatings usually do not give a very good cathodic corrosion protection.
  • the object is to provide a method for producing a hardened profile component with a cathodic corrosion protection, wherein the cathodic corrosion protection is formed so that even the starting material has a protective layer which does not convert during the further processing in a negative way.
  • Another object is to provide a cathodic anti-corrosion layer for curable profile components.
  • Another object is to provide a hardened profile component with cathodic corrosion protection.
  • the inventive method provides, on a hardenable steel sheet, a coating of a mixture consisting essentially of zinc and an oxygen affinity element, such as magnesium, silicon, titanium, calcium and aluminum with a content of 0.1 to 15 wt .-% of the Apply oxygen-affine element and heat the coated steel sheet at least partially with the access of oxygen to a temperature above the Austenitmaschinestemperatur the sheet metal alloy and before to reform, wherein the sheet is cooled after sufficient heating and the cooling rate is such that hardening of the sheet metal alloy takes place.
  • a hardened component is obtained from a steel sheet having a good cathodic corrosion protection.
  • the corrosion protection according to the invention for steel sheets, which are first formed and in particular roll-profiled and then subjected to a heat treatment and deformed and thereby hardened, is a cathodic corrosion protection which is essentially based on zinc.
  • 0.1% to 15% of one or more oxygen-containing elements such as magnesium, silicon, titanium, calcium, aluminum, boron and manganese or any mixture or alloy thereof are added to the zinc forming the coating. It has been found that such small amounts of an oxygen affinity element as magnesium, silicon, titanium, calcium, aluminum, boron and manganese cause a surprising effect in this particular application.
  • At least Mg, Al, Ti, Si, Ca, B, Mn are suitable as oxygen-affine elements.
  • aluminum is mentioned below, this is representative of the other elements mentioned.
  • an oxygen-affine element in particular aluminum, an essentially Al 2 O 3 or an oxide of the oxygen-affine element (MgO, CaO, TiO, SiO 2 , B 2 O 3 , MnO) existing, very effective and healing, superficial protective layer.
  • This very thin oxide layer protects the underlying Zn restroom corrosion protection layer even at very high temperatures from oxidation.
  • an approximately two-layer corrosion protection layer is formed, which consists of a cathodically highly effective layer with a high proportion of zinc and a very thin oxidation protection layer of one or more oxides (Al 2 O 3 , MgO , CaO, TiO, SiO 2 , B 2 O 3 , MnO) is protected against oxidation and evaporation.
  • a cathodic corrosion protection layer with a superior chemical resistance.
  • This means that the heat treatment has to take place in an oxidizing atmosphere. Although under protective gas (oxygen-free atmosphere) oxidation can be avoided, the zinc would evaporate due to the high vapor pressure.
  • a zinc alloy with a content of aluminum in weight percent of greater than 0.1 but less than 15%, in particular less than 10%, more preferably less than 5% on a Steel sheet, in particular an alloyed steel sheet are applied, where in a second step, the sheet is formed inline as a strand and heated in the presence of atmospheric oxygen to a temperature above the Austenitmaschinestemperatur the sheet metal alloy and then cooled at an increased rate.
  • a thin barrier phase is formed, in particular Fe 2 Al 5 -x Zn x , which forms the Fe-Zn Diffusion in a liquid metal coating process, which takes place in particular at a temperature up to 690 ° C, hindered.
  • the sheet is formed with a zinc-metal coating with an addition of aluminum, which is effective only towards the sheet surface, as in the proximal region of the support an extremely thin barrier phase, which is effective against rapid growth of an iron-zinc compound phase, having.
  • the metal layer on the sheet is liquefied for the time being.
  • the oxygen-containing aluminum from the zinc reacts with atmospheric oxygen to form solid oxide, thereby causing a decrease in the aluminum metal concentration, which causes a steady diffusion of aluminum towards depletion, that is to the distal region.
  • This Tonerdeanreichtation, at the air exposed layer area now acts as oxidation protection for the layer metal and as Abdampfungssperre for the zinc.
  • the aluminum is withdrawn from the proximal blocking phase by continuous diffusion towards the distal region and is available there for the formation of the superficial Al 2 O 3 layer.
  • the formation of a sheet metal coating is achieved, which leaves a cathodically highly effective layer with a high zinc content.
  • Well suited is, for example, a zinc alloy with a content of aluminum in weight percent of greater than 0.2 but less than 4, preferably greater than 0.26 but less than 2.5 wt .-%.
  • the zinc alloy layer is applied to the sheet surface passing through a liquid metal bath at a temperature higher than 425 ° C, but lower than 690 ° C, especially at 440 ° C to 495 ° C, followed by cooling of the coated sheet, not only the proximal barrier phase can be effectively formed, or a very good diffusion inhibition can be observed in the region of the barrier layer, but it also takes place to improve the thermoforming properties of the sheet material.
  • An advantageous embodiment of the invention is given in a method in which a hot or cold rolled steel strip having a thickness of for example greater than 0.15 mm and having a concentration range of at least one of the alloying elements within the limits in wt .-% carbon to 0.4, preferably 0.15 to 0.3 silicon to 1.9, preferably 0.11 to 1.5 manganese to 3.0, preferably 0.8 to 2.5 chrome to 1.5, preferably 0.1 to 0.9 molybdenum to 0.9, preferably 0.1 to 0.5 nickel to 0.9, titanium to 0.2 preferably 0.02 to 0.1 vanadium to 0.2 tungsten to 0.2, aluminum to 0.2, preferably 0.02 to 0.07 boron to 0.01, preferably 0.0005 to 0.005 sulfur Max. 0.01, preferably max. 0.008 phosphorus Max. 0.025, preferably max. 0.01 Rest iron and impurities is used.
  • the surface structure of the cathodic corrosion protection according to the invention is particularly favorable for a high adhesion of paints and varnishes.
  • the strip-form provided starting material with the coating according to the invention is fed to a roll forming unit and formed into a rolled section, wherein the rolled section is deformed during roll forming and subsequently cut to length in a cutting unit to the profile components.
  • at least partial areas of the rolled section after leaving the rolling profiling unit or heated to a temperature required for curing prior to entry into the roll forming unit and quenched prior to being cut to length in a cooling unit.
  • the required heating takes place, for example, inductively.
  • starting material provided in strip form is fed to a roll forming unit and converted into a rolled section in the roll forming unit, wherein the rolled section is deformed during roll forming and then the rolled section is cut to length in a cutting unit to the profile components. Subsequently, the already cut to length profiles are stored in a profile memory with separation and then subjected to the hardening step by heating and cooling.
  • a further advantageous embodiment provides for subjecting the separated profiles to an intermediate heat stage prior to curing under oxygen access, wherein in the intermediate heat stage an advantageous change in the corrosion protection layer takes place and only then to a temperature required for curing.
  • the latter can be done with band material as well as with cut profiles.
  • open and closed profiles can be produced by inductive high frequency welding, laser welding, spot welding, seam welding, projection welding and rolling technology.
  • a profile component according to the invention with cathodic protection against corrosion was subsequently produced, as explained below, subsequently subjected to a heat treatment for hardening the profile component and rapid cooling. Subsequently, the sample was analyzed for optical and electrochemical properties. Assessment criteria were the appearance of the annealed sample and the protection energy.
  • the protection energy is the measure for the electrochemical protection of the layer, which is determined by galvanostatic detachment.
  • the electrochemical method of galvanostatic dissolution of the metallic surface coatings of a material allows to classify the mechanism of corrosion protection of the layer.
  • the potential-time behavior of a corrosion-protective layer is determined for a given constant current flow. For the measurements, a current density of 12.7 mA / cm 2 was specified.
  • the measuring arrangement is a three-electrode system.
  • the counterelectrode used was a platinum network, the reference electrode consisting of Ag / AgCl (3M).
  • the electrolyte consists of 100 g / l ZnSO 4 .5H 2 O and 200 g / l NaCl dissolved in deionized water.
  • the barrier protection is characterized by the fact that it separates the base material from the corrosive medium.
  • a steel sheet is hot dip galvanized with a melt consisting of 95% zinc and 5% aluminum.
  • the coated steel sheet is then roll-profiled in a profiling device. After annealing, the sheet shows a silvery-gray surface with no defects.
  • cross section FIG. 7 shows that the coating consists of a light phase and a dark phase, wherein the phases are Zn-Fe-Al-containing phases.
  • the bright phases are more zinc-rich, the dark phases more iron-rich.
  • the galvanostatic dissolution shows a potential of about -0.7 V required for the resolution. This value is significantly below the potential of the steel. After a measuring time of approx. 1,000 seconds, a potential of approx. -0.6 V arises. This potential is also clearly below the steel potential. After a measurement time of approximately 3,500 seconds, this part of the layer is used up and the necessary potential for dissolving the layer approaches the steel potential. This coating thus offers after the annealing in addition to the barrier protection a cathodic corrosion protection.
  • the potential is up to a measuring time of 3,500 seconds at a value of ⁇ -0.6 V, so that a considerable cathodic protection is maintained over a long time, even if the sheet was fed to the austenitizing temperature.
  • the potential time diagram is in FIG. 8 shown.
  • the sheet is passed through a melt or through a zinc bath, with a zinc content of 99.8% and an aluminum content of 0.2%.
  • the coated steel sheet is then roll profiled in a profiling.
  • Aluminum present in the zinc coating reacts with atmospheric oxygen during the calcination and forms a protective Al 2 O 3 skin. Through constant diffusion of the oxygen-affinity aluminum to the surface, this protective skin is maintained and expanded.
  • inductive heating of the sheet shows a silvery-gray surface without defects. From the originally about 15 microns thick zinc coating develops during the annealing due to diffusion, a about 20 to 25 microns thick layer, said layer ( FIG.
  • the annealed material has a potential of approx. -0.75 V. After a measuring time of approx. 1,500 seconds, the potential required for the resolution increases to ⁇ -0.6 V. The phase lasts up to a measuring time of approx. 2,800 seconds. Then the required potential increases to steel potential. In this case too, in addition to barrier protection, there is cathodic corrosion protection. The potential is up to a measurement time of 2,800 seconds at a value of ⁇ -0.6 V. Thus, such a material has thus over a very long time a cathodic protection against corrosion.
  • the potential time diagram is FIG. 10 refer to.
  • This anticorrosive layer contains some aluminum in the zinc bath, of the order of about 0.13%.
  • the profile component is heated to a temperature of about 500 ° C prior to austenitizing.
  • the zinc layer is completely converted into Zn-Fe phases.
  • the zinc layer is thus wholly, i. converted to Zn-Fe phases to the surface. This results in zinc-rich phases on the steel sheet, all of which are formed with a Zn-Fe ratio of> 70% zinc.
  • This anticorrosive layer contains some aluminum in the zinc bath, of the order of about 0.13%.
  • the profile component with the aforementioned fully converted coating is inductively heated to> 900 ° C.
  • the result is a yellow-green surface.
  • the yellow-green surface indicates oxidation of the Zn-Fe phases during annealing.
  • An aluminum oxide protective layer is undetectable. The reason for the absence of an aluminum oxide protective layer can be explained by the fact that in the annealing treatment the aluminum does not migrate as quickly to the surface due to solid Zn-Fe phases and can protect the Zn-Fe coating from oxidation. When heating this material at temperatures around 500 ° C is still no liquid zinc-rich phase, because this forms only at higher temperatures of 782 ° C. If 782 ° C are reached, thermodynamically there is a liquid zinc-rich phase in which the aluminum is freely available. Nevertheless, the surface layer is not protected against oxidation.
  • the corrosion protection layer is already partially oxidized at this time and no opaque aluminum oxide skin can form any more.
  • the layer shows wavy rugged in cross-section and consists of Zn and Zn-Fe oxides ( FIG. 11 ).
  • the surface of said material is much larger due to the highly crystalline acicular surface finish of the surface, which could also be detrimental to the formation of a covering and thicker aluminum oxide protective layer.
  • the said non-inventive coating forms a brittle layer which is provided with numerous cracks, both transversely and longitudinally to the coating. As a result, in the course of the heating, both decarburization and oxidation of the steel substrates can take place, especially with cold preformed components.
  • a profile component made of a sheet metal with a galvanizing as in Example 3 is subjected after the roll forming a particular short, inductive heat treatment, at about 490 ° C to 550 ° C, the zinc layer is only partially converted into Zn-Fe phases.
  • the process is carried out in such a way that the phase transformation is only partially carried out and therefore not yet converted zinc with aluminum on the surface is present and thus free aluminum as oxidation protection for the zinc layer is available.
  • the profile component with the heat-treated coating according to the invention and only partially converted into Zn-Fe phases is subsequently heated inductively to the required austenitizing temperature.
  • the result is a surface that is gray and without defects.
  • a SEM / EDX examination of the cross section shows an approximately 20 microns thick surface layer, wherein from the originally about 15 microns thick zinc coating of the coating has formed in the inductive annealing due to diffusion, an about 20 microns Zn-Fe layer, said layer with the typical for the invention two-phase structure a "leopard pattern" with a gray phase in the image with a composition Zn / Fe of about 30/70 and light areas with the composition Zn / Fe of about 80/20. In addition, individual areas with zinc contents ⁇ 90% zinc are present. On the surface, a protective layer of aluminum oxide is detectable.
  • both barrier protection and very good cathodic corrosion protection can therefore be achieved form. Even with this material, the cathodic protection against corrosion can be maintained over a very long measuring time.
  • the cathodic corrosion protection is negligible with a voltage difference of 100 mV to the steel potential in poorly conducting electrolytes. Although there is still a cathodic corrosion protection even with a smaller difference to the steel potential, if a current is detected when using a steel electrode, but this is negligible for practical aspects, since the corrosive medium must conduct very well, so this contribution to the cathodic Corrosion protection can be used.
  • the area between the potential curve at the galvanostatic dissolution and the specified threshold value of 100 mV was set below the steel potential ( FIG. 8 ). Only the area below the threshold is taken into account. The overlying surface contributes negligibly little or not at all to the cathodic corrosion protection and is therefore not included in the evaluation.
  • cathodic corrosion protection in the context of the invention is subsequently determined that at 15 microns thick coatings and the process and experimental conditions described at least a cathodic corrosion protection energy of 4 J / cm 2 is present.
  • a zinc layer which has been deposited electrolytically on the steel sheet surface is not in itself capable of providing a corrosion protection according to the invention, even after a heating step above the austenitizing temperature.
  • the anticorrosive coatings according to the invention were mentioned for profiling a profiled strand or for roll forming and the subsequent hardening of such a profiled strand or profiled strand sections.
  • the coatings according to the invention or, according to the invention, for a sheet-metal component which must be subjected to a heating step are also suitable for other processes in which a steel sheet should first be provided with a corrosion protection layer, and the thus coated steel sheet is then subjected to a heating step for curing the same and before the heating, in the heating or after heating, a deformation of the sheet is to take place.
  • the fundamental advantage of the layer is that a heated component does not have to be descaled after heating and, moreover, that a very good cathodic corrosion protection layer with a very high corrosion protection energy is available.
  • the profile component according to the invention is produced in that a band is first passed through a forward punch and then inserted into the profiling machine.
  • the strip is bent to a desired profile.
  • the necessary welding is carried out in a welding device.
  • the heating device being, for example, an induction coil.
  • the profile is heated at least partially to an austenitizing temperature necessary for hardening.
  • the cooling takes place.
  • a special cooling is used which prevents the partially liquid surface layer is fused. This causes high cooling rates with low fluid pressure.
  • the special cooling mimics the immersion of the profile in a water bath, with a very large amount of water at low pressure on all sides led to the profile.
  • an additional heating device for the induction heating device which serves to heat the sheet to the austenitizing temperature, which leads the sheet to the first heating stage at approximately 550 ° C.
  • This can be, for example, an induction heating device to which - in order to comply with the necessary periods of time - an isolated region, for example an insulated tunnel region, is connected.
  • the cooling is followed by a calibration device, which subjects the heated and quenched profile strand to a calibration, whereupon the profile strand is then cut to length using a cutting unit.
  • band is drawn off from a strip preparation section and punched in a forward punch in a soft state and then profiled or bent and shaped accordingly in a profiling machine.
  • a welding device may also follow the profiling.
  • the thus preformed profile strand is then cut with a cutting unit or cutting device to the appropriate lengths and transferred to a profile memory with separation.
  • a multiplicity of profiles in particular a multiplicity of profiles of different cross sections which are also formed differently, are stored. From the profile memory with separation the desired profiles are subtracted and fed via a drive roller set the hardness level.
  • the individual profiles are heated with an inductive heating already described to the temperature necessary for curing and subsequently quenched in the form already described, that is gently.
  • the cured profiles can be retrofitted on a straightening scaffold.
  • a heat treatment of the coating is performed prior to heating to the temperature required for curing.
  • the profile is first heated to a temperature necessary for the heat treatment in particular 550 ° C. This heating can be done relatively quickly in an inductive heating stage, wherein, if necessary, the heat of the component for a certain time in an insulating region, for example, an insulated tunnel through which the profiles are performed is maintained.
  • the profiled and finished molded profile strands are cut to standard profile lengths and then transferred to the profile memory with separation, the profile memory stores there exclusively tubes and profiles of a certain length, for example 6m. Depending on the required profile, the profiles are then removed individually and fed to the appropriate further treatment. Even with these profiles, if necessary, a hole pattern can already be arranged.
  • the profiling and in particular the arrangement of the hole pattern can be such that the thermal expansion is fully taken into account during the heat treatment and / or heating to the temperature necessary for curing, so that the component after quenching with respect to the dimensional and Position tolerances is made accurately.
  • a profile component made of sheet steel which has a cathodic protection against corrosion, which reliably remains even when the sheet is heated above the austenitizing temperature. It is also advantageous that the components do not have to be reworked after curing.

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Claims (34)

  1. Procédé pour fabriquer un composant profilé durci à partir d'un alliage d'acier durcissable avec une protection cathodique anticorrosion, dans lequel
    a) on applique un revêtement sur une tôle en alliage d'acier durcissable, de sorte que
    b) le revêtement est essentiellement constitué de zinc, et
    c) le revêtement contient en outre un ou plusieurs éléments ayant une affinité pour l'oxygène, dans une quantité totale de 0,1 à 15 % en poids, par référence à la totalité de revêtement, et
    d) la tôle d'acier revêtue est ensuite profilée par galetage dans un dispositif de profilage de telle façon que la bande de tôle est mise en forme en une barre profilée formée par galetage, et
    e) la rôle d'acier revêtue est ensuite amenée au moins dans des zones partielles avec admission d'oxygène atmosphérique à une température d'austénitisation nécessaire pour le durcissement et est chauffée jusqu'à une modification de structure nécessaire pour le durcissement, dans lequel
    f) il se forme sur le revêtement une peau de surface en un oxyde de l'élément ou des éléments ayant une affinité pour l'oxygène, et
    g) après chauffage suffisant, la tôle est refroidie et la vitesse de refroidissement est choisie de telle façon que l'on obtient un durcissement de l'alliage de la tôle, et
    h) la barre profilée est mise à longueur en portions de barre profilée avant ou après le durcissement,
    i) on exécute avant le profilage et avant la mise à longueur et avant le chauffage à la température nécessaire pour le durcissement, des trous, des évidements, des poinçonnements et/ou un motif de trous nécessaire dans la barre profilée, et
    j) le refroidissement est exécuté avec de l'eau de telle sorte que l'on amène un volume important d'eau sous faible pression sur le composant à durcir.
  2. Procédé selon la revendication 1, caractérisé en ce que la barre profilée réalisée dans le dispositif de profilage est soudée dans un dispositif de soudage successif.
  3. Procédé selon l'une des revendications précédentes, caractérisé en ce que la barre profilée ou les portions de barre profilée est/sont chauffée(s), avant le chauffage à la température nécessaire pour le durcissement, dans une étape de chauffage jusqu'à une température et est/sont maintenue(s) à cette température qui permet la formation partielle de phases fer-zinc dans le revêtement.
  4. Procédé selon l'une des revendications précédentes, caractérisé en ce que la barre profilée ou les portions de barre profilée est/sont amenée(s) à une vitesse de chauffage de 50° C à 100° C par seconde jusqu'à une température de 850° C à 950° C, en ce qu'elle(s) est/sont maintenue(s) à cette température pendant au moins cinq secondes, et est/sont ensuite refroidie(s) à une vitesse de refroidissement de 25° C à 45° C par seconde.
  5. Procédé selon l'une des revendications précédentes, caractérisé en ce que lors du chauffage, la barre profilée ou les portions de barre profilée est/sont maintenue(s) vers 500° C à 600° C, en particulier 530° C à 580° C pendant au moins 10 secondes, et est/sont ensuite encore chauffée(s).
  6. Procédé selon l'une des revendications précédentes, caractérisé en ce que la barre profilée et/ou les portions de barre profilée est/sont chauffée(s) par voie inductive et/ou par rayonnement.
  7. Procédé selon l'une des revendications précédentes, caractérisé en ce que l'on utilise comme élément ayant une affinité pour l'oxygène dans le mélange, du magnésium et/ou du silicium et/ou du titane et/ou du calcium et/ou de l'aluminium et/ou du manganèse et/ou du bore.
  8. Procédé selon l'une des revendications précédentes, caractérisé en ce que le revêtement est appliqué dans un procédé au trempé dans un bain en fusion, dans lequel on utilise un mélange composé essentiellement de zinc avec le ou les éléments ayant une affinité pour l'oxygène.
  9. Procédé selon la revendication 1 et/ou 2, caractérisé en ce que l'on utilise 0,2 à 5 % en poids des éléments ayant une affinité pour l'oxygène.
  10. Procédé selon l'une des revendications précédentes, caractérisé en ce que l'on utilise 0,26 % à 2,5 % en poids des éléments ayant une affinité pour l'oxygène.
  11. Procédé selon l'une des revendications précédentes, caractérisé en ce que l'on utilise essentiellement de l'aluminium à titre d'élément ayant une affinité pour l'oxygène.
  12. Procédé selon l'une des revendications précédentes, caractérisé en ce que le mélange de revêtement est choisi de telle façon que la couche forme pendant le chauffage en surface une peau d'oxyde formée d'oxydes du ou des éléments ayant une affinité pour l'oxygène, et le revêtement forme au moins deux phases, telles qu'il se forme une phase riche en zinc et une phase riche en fer.
  13. Procédé selon l'une des revendications précédentes, caractérisé en ce que la phase riche en fer présente un rapport zinc/fer au maximum de 0,95 (Zn/Fe≤0,95), de préférence de 0,20 à 0,80 (Zn/Fe=0,20 à 0,80), et la phase riche en zinc présente un rapport zinc/fer d'au moins 2,0 (Zn/Fe>2,0), de préférence de 2,3 à 19,0 (Zn/Fe=2,3 à 19,0).
  14. Procédé selon l'une des revendications précédentes, caractérisé en ce que la phase riche en fer présente un rapport zinc/fer d'environ 30:70, et la phase riche en zinc est réalisée avec un rapport zinc/fer d'environ 80:20.
  15. Procédé selon l'une des revendications précédentes, caractérisé en ce que la couche contient en outre des zones individuelles avec des proportions de zinc > 90 %.
  16. Procédé selon l'une des revendications précédentes, caractérisé en ce que le revêtement est réalisé de telle façon que vers une épaisseur de 15 µm après chauffage il se développe un effet de protection cathodique d'au moins 4J/cm2.
  17. Procédé selon l'une des revendications précédentes, caractérisé en ce que le revêtement avec le mélange de zinc et du ou des éléments ayant une affinité pour l'oxygène a lieu en continu à travers un bain de métal liquide à une température de 425° C à 690° C, avec refroidissement successif de la tôle revêtue.
  18. Procédé selon l'une des revendications précédentes, caractérisé en ce que le revêtement avec le mélange de zinc et des éléments ayant une affinité pour l'oxygène a lieu en continu à travers un bain de métal liquide à une température de 440° C à 495° C, avec refroidissement successif de la tôle revêtue.
  19. Procédé selon l'une des revendications précédentes, caractérisé en ce que la tôle est chauffée par voie inductive.
  20. Procédé selon l'une des revendications précédentes, caractérisé en ce que la tôle est chauffée dans un four à rayonnement.
  21. Procédé selon l'une des revendications précédentes, caractérisé en ce que la mise en forme et le durcissement du composant ont lieu avec un dispositif de mise en forme par galetage, tel que la tôle revêtue est chauffée au moins partiellement à la température d'austénitisation, que la tôle est formée par galetage avant, pendant et/ou après et, à la suite de la mise en forme par galetage, elle est refroidie à une vitesse de refroidissement qui provoque un durcissement de l'alliage de la tôle.
  22. Couche de protection anticorrosion pour des profilés mis en forme par galetage en tôle d'acier qui a été soumise à une opération de durcissement, telle que la couche de protection anticorrosion est soumise, après l'application sur la tôle d'acier, à un traitement à chaud sous admission d'oxygène, et lors du chauffage, la tige profilée ou les portions de tige profilée est/sont maintenue(s) vers 500° C à 600° C, en particulier 530° C à 580° C pendant au moins 10 secondes, et est/sont ensuite encore chauffée(s), de sorte que le revêtement est essentiellement constitué de zinc, et contient en outre un ou plusieurs éléments ayant une affinité pour l'oxygène, dans une quantité totale de 0,1 % en poids à 15 % en poids, par référence à la totalité du revêtement, et la couche de protection anticorrosion possède en surface une peau d'oxyde couvrante formée d'oxyde du ou des éléments ayant une affinité pour l'oxygène, et le revêtement forme au moins deux phases, de sorte que l'on réalise une phase riche en zinc et une phase riche en fer.
  23. Couche de protection anticorrosion selon la revendication 26, caractérisée en ce que la couche de protection anticorrosion contient dans le mélange à titre d'élément ayant une affinité pour l'oxygène, du magnésium et/ou du silicium et/ou du titane et/ou du calcium et/ou de l'aluminium et/ou du bore et/ou du manganèse.
  24. Couche de protection anticorrosion selon la revendication 26 et/ou 27, caractérisée en ce que la couche de protection anticorrosion est une couche de protection anticorrosion appliquée dans un procédé par plongée dans un bain de métal liquide.
  25. Couche de protection anticorrosion selon l'une des revendications 26 à 31, caractérisée en ce que les éléments ayant une affinité pour l'oxygène sont contenus dans une quantité totale de 0,1 à 15,0 % en poids.
  26. Couche de protection anticorrosion selon l'une des revendications 26 à 31, caractérisée en ce que ces éléments ayant une affinité pour de l'oxygène sont contenus dans une quantité totale de 0,02 à 0,5 % en poids par référence à la totalité du revêtement.
  27. Couche de protection anticorrosion selon l'une des revendications 26 à 33, caractérisée en ce que les éléments ayant une affinité pour l'oxygène sont contenus dans une quantité totale de 0,6 à 2,5 % en poids.
  28. Couche de protection anticorrosion selon l'une des revendications 26 à 34, caractérisée ce qu'elle contient essentiellement de l'aluminium à titre d'élément ayant une affinité pour l'oxygène.
  29. Couche de protection anticorrosion selon l'une des revendications 26 à 35, caractérisée en ce que la phase riche en fer présente un rapport zinc/fer au maximum de 0,95 (Zn/Fe <0,95) de préférence de 0,20 à 0,80 (Zn/Fe=0,20 à 0,80) et la phase riche en zinc présente un rapport zinc/fer d'au moins 2,0 (Zn/Fe>2,0), de préférence de 2,3 à 19,0 (Zn/Fe=2,3 à 19,0).
  30. Couche de protection anticorrosion selon l'une des revendications 26 à 36, caractérisée en ce que la phase riche en fer présente un rapport zinc/fer d'environ 30:70, et la phase riche en zinc présente un rapport zinc/fer d'environ 80:20
  31. Couche de protection anticorrosion selon l'une des revendications 26 à 37, caractérisée en ce que la couche de protection anticorrosion contient en outre des zones individuelles avec des proportions de zinc > 90 % en poids.
  32. Couche de protection anticorrosion selon l'une des revendications 26 à 38, caractérisée en ce que la couche de protection anticorrosion possède, pour une épaisseur de 15 µm, une énergie protectrice cathodique d'au moins 4 J/cm2.
  33. Composant profilé durci en un alliage d'acier durcissable avec une couche de protection anticorrosion cathodique, dans lequel :
    a) un revêtement est appliqué sur une tôle d'un alliage d'acier durcissable,
    b) le revêtement est essentiellement constitué de zinc, et
    c) le revêtement contient en outre un ou plusieurs éléments ayant une affinité pour l'oxygène dans une quantité totale de 0,1 à 15 % en poids, par référence à la totalité du revêtement, et
    d) la tôle d'acier revêtue est ensuite profilée par galetage dans un dispositif de profilage de telle sorte que la bande de tôle est mise sous la forme d'une barre profilée formée par galetage, et
    e) la tôle d'acier revêtue est ensuite amenée, au moins dans des régions partielles, à une température d'austénitisation nécessaire pour le durcissement sous apport d'oxygène atmosphérique, et est réchauffée jusqu'à une modification de structure nécessaire pour le durcissement,
    f) une peau superficielle en un oxyde du ou des éléments ayant une affinité pour l'oxygène est formée sur le revêtement, et
    g) après réchauffement suffisant, la tôle est refroidie, la vitesse de refroidissement étant choisie de telle manière que l'on obtient un durcissement de l'alliage d'acier,
    h) la barre profilée est mise à longueur, avant ou après le durcissement, sous forme de tronçons de barre profilée,
    i) avant le profilage et avant la mise à longueur et avant le chauffage à la température nécessaire pour le durcissement, on ménage des trous, des évidements, des poinçonnages et/ou un motif de trous nécessaire dans la barre profilée ou dans les tronçons de barre profilée,
    j) le refroidissement est exécuté avec de l'eau, de sorte que l'on amène un volume important d'eau sous faible pression vers le composant à durcir, et
    k) la couche de protection anticorrosion possède, pour une épaisseur de 15 µm, une énergie de protection cathodique d'au moins 4 J/cm2.
  34. Composant en acier durci selon la revendication 40, dans lequel le composant est réalisé à partir d'une bande d'acier laminée à froid avec une épaisseur > 0,15 mm, et avec une plage de concentration de l'un au moins des éléments d'alliage dans les limites suivantes, exprimées en pourcentage en poids :
    carbone, jusqu'à 0,4, de préférence 0,15 à 0,3
    silicium, jusqu'à 1,9, de préférence 0,11 à 1,5
    manganèse, jusqu'à 3,0, de préférence 0,8 à 2,5
    chrome, jusqu'à 1,5, de préférence 0,1 à 0,9
    molybdène, jusqu'à 0,9, de préférence 0,1 à 0,5
    nickel, jusqu'à 0,9
    titane, jusqu'à 0,2, de préférence 0,02 à 0,1
    vanadium, jusqu'à 0,2
    tungstène, jusqu'à 0,2
    aluminium, jusqu'à 0,2, de préférence 0,02 à 0,07
    bore, jusqu'à 0,01, de préférence 0,0005 à 0,005
    soufre, au maximum 0,01, de préférence au maximum 0,008
    phosphore, au maximum 0,025, de préférence au maximum 0,01
    le reste étant du fer et des impuretés.
EP04736386.6A 2003-07-29 2004-06-09 Procede de production d'un element constitutif profile trempe Expired - Lifetime EP1660693B1 (fr)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
AT0120303A AT412878B (de) 2003-07-29 2003-07-29 Korrosionsgeschütztes stahlblechteil mit hoher festigkeit
AT12022003A AT412403B (de) 2003-07-29 2003-07-29 Korrosionsgeschütztes stahlblech
PCT/EP2004/006250 WO2005021820A1 (fr) 2003-07-29 2004-06-09 Procede de production d'un element constitutif profile trempe

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EP1660693A1 EP1660693A1 (fr) 2006-05-31
EP1660693B1 true EP1660693B1 (fr) 2014-09-17

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EP20090015813 Expired - Lifetime EP2177641B1 (fr) 2003-07-29 2004-06-09 Tôle d'acier comprenant une revetement contre la corrosion a base de zinc
EP04736386.6A Expired - Lifetime EP1660693B1 (fr) 2003-07-29 2004-06-09 Procede de production d'un element constitutif profile trempe
EP04739755.9A Expired - Lifetime EP1658390B1 (fr) 2003-07-29 2004-06-09 Procede de production d'un element constitutif en acier trempe
EP20040739756 Expired - Lifetime EP1651789B1 (fr) 2003-07-29 2004-06-09 Procede de production d'elements constitutifs en tole d'acier trempe

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3159419A1 (fr) 2015-10-21 2017-04-26 Voestalpine Krems Gmbh Procédé de fabrication des profiles laminés partiellement durcis

Families Citing this family (110)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE10333165A1 (de) * 2003-07-22 2005-02-24 Daimlerchrysler Ag Pressgehärtetes Bauteil und Verfahren zur Herstellung eines pressgehärteten Bauteils
CN1829817B (zh) * 2003-07-29 2015-01-07 沃斯特阿尔派因钢铁有限责任公司 制造硬化钢零件的方法
US20100199738A1 (en) * 2004-08-13 2010-08-12 Vip Tooling, Inc., (An Indiana Corporation) Modular extrusion die tools
US7685907B2 (en) * 2004-08-13 2010-03-30 Vip Tooling, Inc. Method for manufacturing extrusion die tools
DE102005041741B4 (de) * 2005-09-02 2010-03-18 Daimler Ag Verfahren zum Herstellen eines pressgehärteten Bauteils
JP4690848B2 (ja) * 2005-10-13 2011-06-01 新日本製鐵株式会社 外観、加工性、溶接性に優れた高張力溶融Ｚｎめっき鋼材及びその製造方法
WO2007048883A1 (fr) * 2005-10-27 2007-05-03 Usinor Procede de fabrication d'une piece a tres hautes caracteristiques mecaniques a partir d'une tole laminee et revetue
US20100057254A1 (en) * 2006-11-13 2010-03-04 Salamanca Hugo P Methods for using robotics in mining and post-mining processing
DE102005059614A1 (de) * 2005-12-12 2007-06-14 Nano-X Gmbh Beschichtungsmaterial zum Schutz von Metallen, insbesondere Stahl, vor Korrosion und/oder Verzunderung, Verfahren zum Beschichten von Metallen und Metallelement
SE531379C2 (sv) * 2006-06-08 2009-03-17 Nord Lock Ab Metod för att härda och belägga stålbrickor för låsning samt stållåsbricka
MX2009008557A (es) * 2007-02-23 2009-08-21 Corus Staal Bv Metodo para conformacion termomecanica de un producto final con una tenacidad muy alta y producto elaborado por el mismo.
DE102007013739B3 (de) * 2007-03-22 2008-09-04 Voestalpine Stahl Gmbh Verfahren zum flexiblen Walzen von beschichteten Stahlbändern
DE102007022174B3 (de) * 2007-05-11 2008-09-18 Voestalpine Stahl Gmbh Verfahren zum Erzeugen und Entfernen einer temporären Schutzschicht für eine kathodische Beschichtung
WO2008104610A1 (fr) * 2007-07-19 2008-09-04 Corus Staal Bv Procédé de recuisson d'une bande d'acier ayant une épaisseur variable, dans le sens longitudinal
JP5425770B2 (ja) * 2007-07-19 2014-02-26 タタ、スティール、アイモイデン、ベスローテン、フェンノートシャップ 長さ方向において厚さが変化する鋼ストリップ
DE102007038215A1 (de) 2007-08-13 2009-02-19 Nano-X Gmbh Verfahren zur Herstellung einer aktiven Korrosionsschutzbeschichtung auf Bauteilen aus Stahl
DE102007038214A1 (de) 2007-08-13 2009-02-19 Volkswagen Ag Verfahren zum Korrosionsschutz von Karosserie-, Fahrwerks-, Motorbauteilen oder Abgasanlagen
EP2025771A1 (fr) * 2007-08-15 2009-02-18 Corus Staal BV Procédé de production de bande d'acier revêtu pour produire des éléments taylorisés adaptés à la mise en forme thermomécanique, bande produite, et utilisation d'une telle bande revêtue
JP2009061473A (ja) * 2007-09-06 2009-03-26 Sumitomo Metal Ind Ltd 高強度部品の製造方法
DE102007043154B4 (de) 2007-09-11 2017-01-26 Voestalpine Krems Gmbh Verfahren und Vorrichtung zum Härten von Profilen
DE102007048504B4 (de) * 2007-10-10 2013-11-07 Voestalpine Stahl Gmbh Korrosionsschutzbeschichtung für Stahlbleche und Verfahren zum Konditionieren einer Korrosionsschutzbeschichtung
DE102007050907A1 (de) * 2007-10-23 2009-04-30 Benteler Automobiltechnik Gmbh Verfahren zur Herstellung eines gehärteten Blechprofils
SE531689C2 (sv) * 2007-11-26 2009-07-07 Gestamp Hardtech Ab Sätt att framställa en lackerad höghållfast produkt
DE102007061489A1 (de) 2007-12-20 2009-06-25 Voestalpine Stahl Gmbh Verfahren zum Herstellen von gehärteten Bauteilen aus härtbarem Stahl und härtbares Stahlband hierfür
JP2011508066A (ja) * 2007-12-28 2011-03-10 グレイトポイント・エナジー・インコーポレイテッド 触媒ガス化のための石油コークス組成物
KR101122754B1 (ko) * 2008-04-22 2012-03-23 신닛뽄세이테쯔 카부시키카이샤 도금 강판 및 도금 강판의 열간 프레스 방법
DE102008037442B3 (de) * 2008-10-13 2010-02-25 Thyssenkrupp Steel Ag Verfahren zur Bestimmung von Formänderungen eines Werkstücks
MX2011006528A (es) * 2008-12-19 2011-07-13 Tata Steel Ijmuiden Bv Metodo para fabricar una parte recubierta usando tecnicas de formacion en caliente.
JP4825882B2 (ja) * 2009-02-03 2011-11-30 トヨタ自動車株式会社 高強度焼き入れ成形体及びその製造方法
DE102009007909A1 (de) 2009-02-06 2010-08-12 Thyssenkrupp Steel Europe Ag Verfahren zum Herstellen eines Stahlbauteils durch Warmformen und durch Warmformen hergestelltes Stahlbauteil
DE102009016852A1 (de) * 2009-04-08 2010-10-14 Bayerische Motoren Werke Aktiengesellschaft Verfahren zur Herstellung wärmebehandelter Blechformteile aus einem Stahlblechmaterial mit einer Korrosionsschutzbeschichtung und derartiges Blechformteil
CN101985199B (zh) * 2009-07-29 2012-09-05 比亚迪股份有限公司 一种电子产品外壳的制备方法
ATE554190T1 (de) 2009-08-25 2012-05-15 Thyssenkrupp Steel Europe Ag Verfahren zum herstellen eines mit einem metallischen, vor korrosion schützenden überzug versehenen stahlbauteils und stahlbauteil
DE102009051673B3 (de) * 2009-11-03 2011-04-14 Voestalpine Stahl Gmbh Herstellung von Galvannealed-Blechen durch Wärmebehandlung elektrolytisch veredelter Bleche
CN101935789B (zh) * 2009-11-19 2012-03-07 江苏麟龙新材料股份有限公司 含Al-Zn-Si-Mg-RE-Ti-Ni的热浸镀铸铝合金及其制备方法
DE102009056443A1 (de) * 2009-12-02 2011-06-09 Benteler Automobiltechnik Gmbh Crashbox und Verfahren zu deren Herstellung
KR101171450B1 (ko) 2009-12-29 2012-08-06 주식회사 포스코 도금 강재의 열간 프레스 성형방법 및 이를 이용한 열간 프레스 성형품
DE102010004823B4 (de) * 2010-01-15 2013-05-16 Benteler Automobiltechnik Gmbh Verfahren zur Herstellung eines metallischen Formbauteils für Kraftfahrzeugkomponenten
KR101798257B1 (ko) 2010-02-19 2017-11-15 타타 스틸 네덜란드 테크날러지 베.뷔. 열간 성형에 적당한 스트립, 시트 또는 블랭크, 및 이의 제조 방법
DE102010017354A1 (de) * 2010-06-14 2011-12-15 Thyssenkrupp Steel Europe Ag Verfahren zum Herstellen eines warmgeformten und gehärteten, mit einer metallischen Korrosionsschutzbeschichtung überzogenen Stahlbauteils aus einem Stahlflachprodukt
DE102010037077B4 (de) 2010-08-19 2014-03-13 Voestalpine Stahl Gmbh Verfahren zum Konditionieren der Oberfläche gehärteter korrosionsgeschützter Bauteile aus Stahlblech
KR20130099042A (ko) 2010-08-31 2013-09-05 타타 스틸 이즈무이덴 베.뷔. 코팅된 금속 부품과 성형된 부품의 열간 성형 방법
CN103140304B (zh) 2010-09-30 2015-08-19 株式会社神户制钢所 冲压成形品及其制造方法
DE102011053941B4 (de) 2011-09-26 2015-11-05 Voestalpine Stahl Gmbh Verfahren zum Erzeugen gehärteter Bauteile mit Bereichen unterschiedlicher Härte und/oder Duktilität
KR20130132566A (ko) * 2010-12-24 2013-12-04 뵈스트알파인 스탈 게엠베하 경화된 구조적 요소의 제조 방법
DE102011053939B4 (de) 2011-09-26 2015-10-29 Voestalpine Stahl Gmbh Verfahren zum Erzeugen gehärteter Bauteile
DE102011001140A1 (de) * 2011-03-08 2012-09-13 Thyssenkrupp Steel Europe Ag Stahlflachprodukt, Verfahren zum Herstellen eines Stahlflachprodukts und Verfahren zum Herstellen eines Bauteils
US20140004378A1 (en) * 2011-03-18 2014-01-02 Nippon Steel & Sumitomo Metal Corporation Steel sheet for hot stamped member and method of production of same
ES2389188B1 (es) * 2011-03-29 2013-09-02 Rovalma Sa Proteccion catodica mediante recubrimiento para circuitos de refrigeracion u otros agujeros o canales.
DE202011107125U1 (de) 2011-04-13 2011-11-30 Tata Steel Ijmuiden Bv Warmformbares Band, Blech oder Zuschnitt und warmgeformtes Produkt
CN103492600B (zh) * 2011-04-27 2015-12-02 新日铁住金株式会社 热冲压部件用钢板及其制造方法
WO2012167930A1 (fr) * 2011-06-07 2012-12-13 Tata Steel Ijmuiden B.V. Bande, feuille ou ébauche thermoformable, procédé pour sa production, procédé pour thermoformer un produit et produit thermoformé
DE102011108162B4 (de) * 2011-07-20 2013-02-21 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines Bauteils durch Warmumformen eines Vorproduktes aus Stahl
US9677145B2 (en) 2011-08-12 2017-06-13 GM Global Technology Operations LLC Pre-diffused Al—Si coatings for use in rapid induction heating of press-hardened steel
DE102011056444C5 (de) 2011-12-14 2015-10-15 Voestalpine Metal Forming Gmbh Verfahren und Vorrichtung zum partiellen Härten von Blechbauteilen
KR20140107230A (ko) * 2011-12-20 2014-09-04 아크티에볼라게트 에스케이에프 플래쉬 버트 용접에 의해 강재 부품을 제조하기 위한 방법 및 상기 방법에 의해 제조되는 부품
DE102012101018B3 (de) 2012-02-08 2013-03-14 Thyssenkrupp Nirosta Gmbh Verfahren zum Schmelztauchbeschichten eines Stahlflachprodukts
KR101657931B1 (ko) 2012-03-30 2016-09-19 가부시키가이샤 고베 세이코쇼 냉간 가공성, 금형 담금질성 및 표면 성상이 우수한 프레스 성형용 용융 아연도금 강판 및 그의 제조 방법
DE102012024616A1 (de) * 2012-12-17 2014-06-18 GM Global Technology Operations LLC (n. d. Gesetzen des Staates Delaware) Stahlblech und Formteil daraus
DE102013100682B3 (de) * 2013-01-23 2014-06-05 Voestalpine Metal Forming Gmbh Verfahren zum Erzeugen gehärteter Bauteile und ein Strukturbauteil, welches nach dem Verfahren hergestellt ist
DE102013204449A1 (de) * 2013-03-14 2014-09-18 Zf Friedrichshafen Ag Verfahren zur Herstellung eines korrosionsgeschützten Blechteils
KR20160007648A (ko) 2013-05-17 2016-01-20 에이케이 스틸 프로퍼티즈 인코포레이티드 프레스 경화 적용을 위한 아연-코팅된 스틸 및 그 생산 방법
CN103342012B (zh) * 2013-07-08 2015-12-02 湖北交投四优钢科技有限公司 一种渗铝钢板网及制备方法
CN103320745B (zh) * 2013-07-08 2014-01-08 湖北交投四优钢科技有限公司 一种渗铝钢及制备方法
DE102013108046A1 (de) * 2013-07-26 2015-01-29 Thyssenkrupp Steel Europe Ag Verfahren und Vorrichtung zum partiellen Härten von Halbzeugen
CN105018923B (zh) * 2014-04-29 2018-10-02 宝山钢铁股份有限公司 一种覆钛低碳钢复合板制备方法
DE102014210008A1 (de) * 2014-05-26 2015-11-26 Muhr Und Bender Kg Verfahren und Anlage zum Herstellen eines gehärteten Formteils
DE102014109315C5 (de) 2014-07-03 2022-02-24 Thyssenkrupp Ag Verfahren zum Herstellen von Profilen aus Metall
DE102014109553A1 (de) * 2014-07-08 2016-01-14 Thyssenkrupp Ag Härtewerkzeug und Verfahren zum Herstellen gehärteter Profilformteile
US9850553B2 (en) 2014-07-22 2017-12-26 Roll Forming Corporation System and method for producing a hardened and tempered structural member
DE102014110415B4 (de) 2014-07-23 2016-10-20 Voestalpine Stahl Gmbh Verfahren zum Aufheizen von Stahlblechen und Vorrichtung zur Durchführung des Verfahrens
DE102014110564B4 (de) * 2014-07-25 2016-12-22 Thyssenkrupp Ag Verfahren zum Herstellen eines Profils und eine Fertigungsanlage zur Herstellung eines Profils
US20170321314A1 (en) * 2014-11-04 2017-11-09 Voestalpine Stahl Gmbh Method for producing an anti-corrosion coating for hardenable sheet steels and an anti-corrosion coating for hardenable sheet steels
CN104635748B (zh) * 2014-12-18 2017-11-17 温州泓呈祥科技有限公司 冲压式太阳能发电跟踪转盘
CN105296862A (zh) * 2015-02-10 2016-02-03 苏州科胜仓储物流设备有限公司 一种用于穿梭车货架的高强度防腐钢板及其加工工艺
CN104651728A (zh) * 2015-02-10 2015-05-27 苏州科胜仓储物流设备有限公司 一种用于仓储设备的抗腐蚀钢板及其制备方法
DE102015113056B4 (de) 2015-08-07 2018-07-26 Voestalpine Metal Forming Gmbh Verfahren zum kontaktlosen Kühlen von Stahlblechen und Vorrichtung hierfür
JP7141828B2 (ja) 2015-05-29 2022-09-26 フォエスタルピネ スタール ゲーエムベーハー 温度調節されるべき非無端表面の均一な非接触温度調節方法およびその装置
MX2017014559A (es) 2015-06-03 2018-03-15 Salzgitter Flachstahl Gmbh Componente endurecido por deformacion hecho de acero galvanizado, metodo de produccion para el mismo y metodo para producir una tira de acero adecuada para el endurecimiento por deformacion de los componentes.
WO2017017483A1 (fr) 2015-07-30 2017-02-02 Arcelormittal Tôle d'acier revêtue d'un revêtement métallique à base d'aluminium
WO2017017484A1 (fr) 2015-07-30 2017-02-02 Arcelormittal Procédé pour la fabrication d'une pièce durcie qui ne présente pas de problèmes lme (liquide metal embrittlement - fragilité par les métaux liquides)
WO2017017485A1 (fr) 2015-07-30 2017-02-02 Arcelormittal Procédé de fabrication d'une pièce phosphatable à partir d'une tôle d'acier revêtue d'un revêtement métallique à base d'aluminium
EP3162558A1 (fr) 2015-10-30 2017-05-03 Outokumpu Oyj Composant constitué d'un matériau composite métallique et procédé pour la fabrication du composant par formage à chaud
DE102015016656A1 (de) 2015-12-19 2017-06-22 GM Global Technology Operations LLC (n. d. Ges. d. Staates Delaware) Verfahren zur Herstellung eines beschichteten, durch Warmumformung gehärteten Körpers sowie ein nach dem Verfahren hergestellter Körper
DE102016102504A1 (de) 2016-02-08 2017-08-10 Salzgitter Flachstahl Gmbh Aluminiumbasierte Beschichtung für Stahlbleche oder Stahlbänder und Verfahren zur Herstellung hierzu
DE102016102324B4 (de) * 2016-02-10 2020-09-17 Voestalpine Metal Forming Gmbh Verfahren und Vorrichtung zum Erzeugen gehärteter Stahlbauteile
DE102016102322B4 (de) * 2016-02-10 2017-10-12 Voestalpine Metal Forming Gmbh Verfahren und Vorrichtung zum Erzeugen gehärteter Stahlbauteile
DE102016102344B4 (de) * 2016-02-10 2020-09-24 Voestalpine Metal Forming Gmbh Verfahren und Vorrichtung zum Erzeugen gehärteter Stahlbauteile
TWI601849B (zh) * 2016-06-08 2017-10-11 China Steel Corp Method for manufacturing thermoformed zinc-based plated steel sheet and hot stamping method thereof
DE102017214561B4 (de) 2016-08-29 2019-05-16 Magna Powertrain Inc. Verfahren zum Bilden einer Keilverzahnung in einer Komponente unter Verwendung von ultrahochfestem Stahl
US10837072B2 (en) 2016-08-29 2020-11-17 Magna Powertrain Inc. Splined power transmission components made using heat-assisted calibration process and method of forming such splined power transmission components
US10371646B2 (en) * 2016-09-19 2019-08-06 The Boeing Company Method and system for automated data collection and part validation
DE102016122323A1 (de) 2016-11-21 2018-05-24 Illinois Tool Works Inc. Schweißbare Gewindeplatte
PT3360981T (pt) 2017-02-10 2020-10-08 Outokumpu Oy Aço para fabrico de um componente por moldação a quente e utilização do componente
DE102017110864B3 (de) 2017-05-18 2018-10-18 Voestalpine Metal Forming Gmbh Verfahren und Vorrichtung zum Erzeugen gehärteter Stahlblechbauteile mit unterschiedlichen Blechdicken
EP3758889A4 (fr) * 2018-03-01 2021-11-17 Nucor Corporation Aciers durcissables par pression revêtus d'alliage de zinc et leur procédé de fabrication
US10481052B2 (en) 2018-03-28 2019-11-19 Ford Global Technologies, Llc Quality control process to assess the aluminized coating characteristics of hot stamped parts
US11084169B2 (en) * 2018-05-23 2021-08-10 General Electric Company System and method for controlling a robotic arm
KR102176342B1 (ko) * 2018-09-28 2020-11-09 주식회사 포스코 전기강판 제품의 제조 방법
EP3726206B1 (fr) 2019-03-26 2022-11-02 FEI Company Procédés et systèmes d'analyse d'inclusion
US11149327B2 (en) 2019-05-24 2021-10-19 voestalpine Automotive Components Cartersville Inc. Method and device for heating a steel blank for hardening purposes
JP2023510699A (ja) * 2019-12-20 2023-03-15 オートテック エンジニアリング エス．エレ． 物体を成形するための方法及び製造ライン
US12031215B2 (en) 2020-01-29 2024-07-09 Nucor Corporation Zinc alloy coating layer of press-hardenable steel
TWI741613B (zh) * 2020-05-21 2021-10-01 元大興企業有限公司 耐候性型鋼成型設備及耐候性型鋼
CN112011752B (zh) * 2020-08-20 2022-06-21 马鞍山钢铁股份有限公司 一种高耐蚀热成形钢零部件及其制造方法
CN112846665A (zh) * 2021-01-06 2021-05-28 王志刚 轴向金属密封环的生产方法
EP4029964A1 (fr) 2021-01-14 2022-07-20 Hilti Aktiengesellschaft Durcissement d'un corps de vis revêtu de zinc
DE102021123279A1 (de) 2021-09-08 2023-03-09 Voestalpine Metal Forming Gmbh Verfahren zum Erzeugen von gehärteten Stahlblechbauteilen
DE102022107131A1 (de) 2022-03-25 2023-09-28 Voestalpine Metal Forming Gmbh Verfahren und Vorrichtung zum Erzeugen gehärteter Stahlblechbauteile
CN118786228A (zh) 2023-02-10 2024-10-15 奥钢联金属成型有限公司 制备硬化钢部件的方法

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3630792A (en) * 1969-04-28 1971-12-28 Cominco Ltd Process for the production of colored coatings
JPH05148606A (ja) * 1991-11-28 1993-06-15 Nkk Corp プレス成形性およびスポツト溶接性に優れた合金化溶融亜鉛メツキ鋼板の製造方法
JPH0754127A (ja) * 1993-08-09 1995-02-28 Shinto Kogyo Kk 溶融亜鉛めっき装置材料
EP0508479B1 (fr) * 1991-04-10 1995-10-25 Kawasaki Steel Corporation Tôle d'acier entièrement ou partiellement revêtue de zinc ainsi que procédé pour sa fabrication
DE10039375A1 (de) * 2000-08-11 2002-03-28 Fraunhofer Ges Forschung Korrosionsgeschütztes Stahlblech und Verfahren zu seiner Herstellung
EP1288325A1 (fr) * 2000-04-24 2003-03-05 Nkk Corporation Tole d'acier recuit apres galvanisation et procede de production correspondant

Family Cites Families (55)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3791801A (en) * 1971-07-23 1974-02-12 Toyo Kohan Co Ltd Electroplated steel sheet
SE435527B (sv) 1973-11-06 1984-10-01 Plannja Ab Forfarande for framstellning av en detalj av herdat stal
JPS52120252A (en) * 1976-04-02 1977-10-08 Honda Motor Co Ltd Method and device for forging thin plate member
JPS55110783A (en) * 1979-02-15 1980-08-26 Sumitomo Metal Ind Ltd Surface treated steel plate with excellent spot weldability
JPS569386A (en) * 1979-07-02 1981-01-30 Nippon Kokan Kk <Nkk> Production of electro-zinc plated steel plate
JPS58189363A (ja) * 1982-04-26 1983-11-05 Nisshin Steel Co Ltd 合金化亜鉛めつき鋼板の製造方法
FR2534161B1 (fr) 1982-10-06 1985-08-30 Maubeuge Fer Procede et dispositif de production en continu d'une bande metallique galvanisee et profilee
JPS61119693A (ja) * 1984-11-14 1986-06-06 Sumitomo Metal Ind Ltd 積層メツキ鋼板
JPS62142755A (ja) * 1985-12-17 1987-06-26 Nippon Steel Corp 合金化溶融亜鉛めつき鋼板およびその製造方法
JPS6362855A (ja) * 1986-09-03 1988-03-19 Toyota Motor Corp 差厚合金化溶融亜鉛めつき鋼板の製造方法
DE3787347T2 (de) * 1986-11-21 1994-01-13 Nikko Aen Kk Gefärbte Zinkbeschichtung.
US4830683A (en) * 1987-03-27 1989-05-16 Mre Corporation Apparatus for forming variable strength materials through rapid deformation and methods for use therein
BE1001029A3 (nl) * 1987-10-22 1989-06-13 Bekaert Sa Nv Staalsubstraat met metaaldeklagen ter versterking van vulkaniseerbare elastomeren.
JPH01242714A (ja) * 1988-03-25 1989-09-27 Mitsubishi Heavy Ind Ltd 鉄鋼部品の熱処理方法
US4913746A (en) * 1988-08-29 1990-04-03 Lehigh University Method of producing a Zn-Fe galvanneal on a steel substrate
JPH02190483A (ja) * 1989-01-19 1990-07-26 Nippon Steel Corp プレス成形性に優れた亜鉛めっき鋼板
JPH042758A (ja) 1990-04-18 1992-01-07 Nippon Steel Corp プレス成形性及び塗装耐食性に優れた溶融系合金亜鉛めっき鋼板の製造方法
JPH05214544A (ja) * 1991-04-10 1993-08-24 Kawasaki Steel Corp 高耐食性亜鉛系めっき鋼板およびその製造方法
AT402032B (de) * 1991-07-17 1997-01-27 Evg Entwicklung Verwert Ges Maschine zum bearbeiten von gittermatten aus miteinander verschweissten längs- und querdrähten
JPH05171491A (ja) * 1991-12-26 1993-07-09 Sumitomo Metal Ind Ltd 塗装後耐食性に優れた２層めっき鋼材
AT397815B (de) * 1992-03-31 1994-07-25 Voest Alpine Ind Anlagen Verfahren zum verzinken eines bandes sowie anlage zur durchführung des verfahrens
JPH06256925A (ja) 1993-03-08 1994-09-13 Nippon Steel Corp プレス成形性に優れた亜鉛−鉄合金化溶融亜鉛めっき鋼板
JPH08325689A (ja) * 1995-05-30 1996-12-10 Nippon Steel Corp 潤滑性、化成処理性に優れた溶融亜鉛系めっき熱延鋼板の製造設備
JP3345219B2 (ja) 1995-06-15 2002-11-18 酒井医療株式会社 起立訓練ベッド
SE9602257L (sv) * 1996-06-07 1997-12-08 Plannja Hardtech Ab Sätt att framställa ståldetalj
JP3400289B2 (ja) * 1997-03-26 2003-04-28 川崎製鉄株式会社 めっき密着性に優れた合金化溶融亜鉛めっき鋼板の製造方法
IT1291883B1 (it) * 1997-04-18 1999-01-21 Sviluppo Materiali Spa Procedimento per la produzione in continuo, tramite deposizione fisica da fase vapore, di nastri metallici rivestiti con elevata
US6178800B1 (en) * 1998-07-14 2001-01-30 Msp Industries Corporation Zone heating methods and apparatuses for metal workpieces for forging
FR2787735B1 (fr) 1998-12-24 2001-02-02 Lorraine Laminage Procede de realisation d'une piece a partir d'une bande de tole d'acier laminee et notamment laminee a chaud
JP2000336467A (ja) * 1999-03-24 2000-12-05 Kawasaki Steel Corp 溶融亜鉛めっき鋼板およびその製造方法
US6465114B1 (en) * 1999-05-24 2002-10-15 Nippon Steel Corporation -Zn coated steel material, ZN coated steel sheet and painted steel sheet excellent in corrosion resistance, and method of producing the same
JP3675313B2 (ja) * 1999-07-15 2005-07-27 Ｊｆｅスチール株式会社 摺動性に優れた合金化溶融亜鉛めっき鋼板の製造方法
JP2001109121A (ja) 1999-10-06 2001-04-20 Konica Corp ハロゲン化銀写真感光材料用自動現像装置
KR20010039405A (ko) * 1999-10-30 2001-05-15 이계안 아연-철 합금 도금 강판의 제조방법
TW504519B (en) * 1999-11-08 2002-10-01 Kawasaki Steel Co Hot dip galvanized steel plate excellent in balance of strength and ductility and in adhesiveness between steel and plating layer, and method for producing the same
JP2001295015A (ja) * 2000-02-09 2001-10-26 Nisshin Steel Co Ltd 高Ａｌ含有溶融Ｚｎ−Ａｌ−Ｍｇ系めっき鋼板
JP2001264591A (ja) 2000-03-22 2001-09-26 Yasuhiro Koike 光通信用発光複合部品
FR2807447B1 (fr) * 2000-04-07 2002-10-11 Usinor Procede de realisation d'une piece a tres hautes caracteristiques mecaniques, mise en forme par emboutissage, a partir d'une bande de tole d'acier laminee et notamment laminee a chaud et revetue
DE10023312C1 (de) * 2000-05-15 2001-08-23 Thyssenkrupp Stahl Ag Galvannealed-Feinblech und Verfahren zum Herstellen von derartigem Feinblech
JP2001329352A (ja) * 2000-05-19 2001-11-27 Sumitomo Metal Ind Ltd 摺動性に優れた合金化溶融亜鉛めっき鋼板
JP4489273B2 (ja) * 2000-10-02 2010-06-23 本田技研工業株式会社 車体パネルの製造方法
DE10049660B4 (de) 2000-10-07 2005-02-24 Daimlerchrysler Ag Verfahren zum Herstellen lokal verstärkter Blechumformteile
US6939623B2 (en) * 2000-12-19 2005-09-06 Posco High strength steel plate having superior electromagnetic shielding and hot-dip galvanizing properties
KR100455083B1 (ko) * 2000-12-22 2004-11-08 주식회사 포스코 내식성 및 용접성이 우수한 아연-코발트-텅스텐 합금전기도금강판 및 그 도금용액
DE10065495C2 (de) 2000-12-28 2002-11-14 Semikron Elektronik Gmbh Leistungshalbleitermodul
DE10120063C2 (de) 2001-04-24 2003-03-27 Benteler Automobiltechnik Gmbh Verfahren zur Herstellung von metallischen Profilbauteilen für Kraftfahrzeuge
DE10120919A1 (de) 2001-04-27 2002-10-31 Benteler Automobiltechnik Gmbh Verfahren zur Herstellung eines gehärteten Blechprofils
JP3582504B2 (ja) * 2001-08-31 2004-10-27 住友金属工業株式会社 熱間プレス用めっき鋼板
JP3582512B2 (ja) * 2001-11-07 2004-10-27 住友金属工業株式会社 熱間プレス用鋼板およびその製造方法
KR100646619B1 (ko) * 2001-10-23 2006-11-23 수미도모 메탈 인더스트리즈, 리미티드 열간 프레스 방법, 이를 위한 도금 강철재 및 이의 제조방법
DE10209264B4 (de) * 2002-03-01 2005-06-02 Ab Skf Verfahren zum Herstellen eines Bauteils aus Metall
DE10254695B3 (de) 2002-09-13 2004-04-15 Daimlerchrysler Ag Verfahren zur Herstellung eines metallischen Formbauteils
DE10246614A1 (de) 2002-10-07 2004-04-15 Benteler Automobiltechnik Gmbh Verfahren zur Herstellung eines beschichteten Strukturbauteils für den Fahrzeugbau
DE10257737B3 (de) * 2002-12-10 2004-02-26 Thyssenkrupp Stahl Ag Verfahren zur elektrolytischen Magnesium-Abscheidung auf verzinktem Blech
CN1829817B (zh) * 2003-07-29 2015-01-07 沃斯特阿尔派因钢铁有限责任公司 制造硬化钢零件的方法

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3630792A (en) * 1969-04-28 1971-12-28 Cominco Ltd Process for the production of colored coatings
EP0508479B1 (fr) * 1991-04-10 1995-10-25 Kawasaki Steel Corporation Tôle d'acier entièrement ou partiellement revêtue de zinc ainsi que procédé pour sa fabrication
JPH05148606A (ja) * 1991-11-28 1993-06-15 Nkk Corp プレス成形性およびスポツト溶接性に優れた合金化溶融亜鉛メツキ鋼板の製造方法
JPH0754127A (ja) * 1993-08-09 1995-02-28 Shinto Kogyo Kk 溶融亜鉛めっき装置材料
EP1288325A1 (fr) * 2000-04-24 2003-03-05 Nkk Corporation Tole d'acier recuit apres galvanisation et procede de production correspondant
DE10039375A1 (de) * 2000-08-11 2002-03-28 Fraunhofer Ges Forschung Korrosionsgeschütztes Stahlblech und Verfahren zu seiner Herstellung

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
SHIH H C ET AL: "The lifetime assessment of hot-dip 5% Al-Zn coatings in chloride environments", SURFACE AND COATINGS TECHNOLOGY, ELSEVIER, AMSTERDAM, NL, vol. 150, 1 February 2002 (2002-02-01), pages 70 - 75, XP002569257, ISSN: 0257-8972, DOI: 10.1016/S0257-8972(01)01508-0 *
WEINBERG F ET AL: "SEGREGATION IN GALFAN HOT DIPPED SHEET STEEL", CANADIAN METALLURGICAL QUARTERLY, TARRYTOWN, NY, US, vol. 29, no. 2, 1 April 1990 (1990-04-01), pages 163 - 166, XP008050261 *

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3159419A1 (fr) 2015-10-21 2017-04-26 Voestalpine Krems Gmbh Procédé de fabrication des profiles laminés partiellement durcis
WO2017067827A1 (fr) 2015-10-21 2017-04-27 Voestalpine Krems Gmbh Procédé de production de profilés roulés partiellement durcis

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JP5054378B2 (ja) 2012-10-24
US20110045316A1 (en) 2011-02-24
JP2007500285A (ja) 2007-01-11
EP1658390A1 (fr) 2006-05-24
PT1651789E (pt) 2010-11-05
US20070000117A1 (en) 2007-01-04
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MXPA06000826A (es) 2006-08-23
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KR100825975B1 (ko) 2008-04-28
CN104372278A (zh) 2015-02-25
KR20060036111A (ko) 2006-04-27
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US20070271978A1 (en) 2007-11-29
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KR100834555B1 (ko) 2008-06-02
DE502004011583D1 (de) 2010-10-07
EP2177641A1 (fr) 2010-04-21
EP1651789A1 (fr) 2006-05-03
US20070256808A1 (en) 2007-11-08
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EP2177641B1 (fr) 2013-04-24
CN1829817A (zh) 2006-09-06
EP1660693A1 (fr) 2006-05-31
BRPI0412601B1 (pt) 2013-07-23
US7832242B2 (en) 2010-11-16
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CN1829816A (zh) 2006-09-06
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US7938949B2 (en) 2011-05-10
ATE478971T1 (de) 2010-09-15
ES2350931T3 (es) 2011-01-28
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ES2421182T3 (es) 2013-08-29
US8021497B2 (en) 2011-09-20

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